Microstructural analysis of cold drawn CuAlMn shapememory alloy wire

Ivanić, Ivana; Kožuh, Stjepan; Pavičić, Nikolina; Čubela, Dijana;Beganović, Omer; Kosec, Borut; Gojić, Mirko

Source / Izvornik: Proceedings book 18th International Foundrymen Conference, 2019, 237 - 246

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University of Zagreb

Faculty of Metallurgy

Sisak, Croatia

University of Ljubljana

Faculty of Natural Sciences and Engineering

Ljubljana, Slovenia

University North

Koprivnica, Croatia

Technical University of Košice

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Košice, Slovakia

ELKEM ASA

Oslo, Norway

PROCEEDINGS BOOK

18th

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CONFERENCE

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technology in economic growth

Sisak, May 15

th – 17

th, 2019

ORGANIZERS

University of Zagreb Faculty of Metallurgy, Sisak, Croatia

University of Ljubljana Faculty of Natural Sciences and Engineering, Ljubljana, Slovenia

University North, Koprivnica, Croatia

Technical University of Košice Faculty of Materials, Metallurgy and Recycling, Košice, Slovakia

ELKEM ASA, Oslo, Norway

PROCEEDINGS BOOK

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EDITORS

Natalija Dolić, Zdenka Zovko Brodarac, Anita Begić Hadžipašić

TECHNICAL EDITOR

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Faculty of Metallurgy

Aleja narodnih heroja 3

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ISBN

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-A CIP record is available in computer catalogue of the National and University Library in Zagreb under the

number 001029655.

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MICROSTRUCTURAL ANALYSIS OF COLD DRAWN CuAlMn SHAPE MEMORY

ALLOY WIRE

Ivana Ivanić1*

, Stjepan Kožuh1, Nikolina Pavičić2, Dijana Čubela3

, Omer Beganović4, Borut

Kosec5, Mirko Gojić1

1 University of Zagreb Faculty of Metallurgy, Sisak, Croatia

2 Master degree student at University of Zagreb Faculty of Metallurgy, Sisak, Croatia

3 University of Zenica Faculty of Metallurgy and Technology, Zenica, Bosnia and Herzegovina

4 University of Zenica Metallurgical Institute Kemal Kapetanović, Zenica, Bosnia and Herzegovina

5 University of Ljubljana Faculty of Natural Sciences and Engineering, Ljubljana, Slovenia

Poster presentation

Original scientific paper

Abstract

The Cu-11.9Al-2.5Mn (wt. %) shape memory alloy was produced by vertically continuous casting

technique obtaining bars of 8 mm in diameter which is applicable for plastic deformation. With the

process of hot rolling and forging the 4.80 mm bar was produced. Afterwards, the obtained 4.80 mm

bar was subjected to cold drawing process. After first run and after fourth run of cold drawing

process the wire with diameter of 4.47 mm and 3.22 mm was produced, respectively. Optical

microscopy (OM) and scanning electron microscopy (SEM) equipped with energy dispersive

spectroscopy (EDS) shown the insight in the samples microstructure. The as-cast state sample has

two phase (α+β) microstructure. After cold working process the two-phase (martensite+α)

microstructure appears. As the result of the cold working process it can be noticed a texture inside

the sample depending on cold drawing direction. The microhardness of samples increases as the

wires diameter decreases.

Keywords: CuAlMn wire, shape memory alloy, microstructure, hot working, cold working

*Corresponding author (e-mail address): iivanic@simet.hr

INTRODUCTION

Cooper based shape memory alloys (SMAs) are very interesting material for industrial

application due to its good shape memory effect (SME), relatively low cost, good

machinability and damping capacity in comparison to the properties that NiTi alloy obtain.

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Its excellent thermal stability and very high martensite transformation temperature makes

them rapidly become one of the most promising high temperature shape memory alloys

[1,2].

CuZnAl and CuAlNi shape memory alloys have been extensively investigated due to its

previously mentioned properties. However, these shape memory alloys are too brittle for

cold working because of coarse grain structure and high elastic anisotropy [3]. The large

grain size problem can be solved by using grain size refinements (as titanium and boron for

example) or production by rapid solidification techniques. This type of production ensures

shaping and forming procedures easier [4-6]. Mechanical properties improvement,

preferably meaning ductility, can be provided by adding alloying elements and by heat

treatment as well [7].

Addition of manganese to binary CuAl alloy can significantly improve alloys properties by

stabilizing the bcc phase, widening the single β-phase region to lower temperatures and

improving ductility in low Al alloys (less than 18 at. %) [8,9]. The austenitic β-phase arranged

to the lower order system β1 (L21; Cu2AlMn) and martensitic phase stabilization of unstable

β´3 (18R) to stable γ´3 (2H) ratio can be adjusted by quenching and the amount of aluminium

(Al) and manganese (Mn) [10].

The CuAlMn alloys exhibit shape memory effect and superelasticity based on cubic β1 (L21)

to monoclinic β1' (6M) martensitic transformation. The shape memory characteristics

(superelasticity and shape memory effect) of CuAlMn SMAs can be enhanced by the addition

of alloying elements and the application of microstructure control achieved by

thermomechanical treatment. It has been reported that those characteristics strongly

depend on grain size and the development of texture [11]. Some investigations have been

demonstrated that low thermal expansion can be obtained in CuAlMn shape memory alloys

by controlling stress-induced martensitic transformation due to cold-rolling [8,11].

Due to the fact that CuAlMn shape memory alloy possesses significant ductility the aim of

this paper is to produce a ductile CuAlMn shape memory alloy wire for possible industrial

application with favorable microstructural properties by hot/cold plastic deformation

process.

MATERIALS AND METHODS

Copper-based SMA with the nominal composition of Cu-11.9Al-2.5Mn (wt. %) was prepared

in a vacuum induction furnace. The bar of 8 mm in diameter (Figure 1) was obtained and it

was used for hot/cold plastic deformation process to obtain wire. Firstly, the bar was

subjected to hot working process which was performed by a combination of hot rolling and

hot forging. The forging was performed as free forging and forging in a profiled tool (Figure

2). The obtained bar after first run of rolling and forging was presented at Figure 3. The

forging and rolling procedures were performed alternately till the cross section of the bar

was 4.80 mm. Afterwards, the obtained bars were taken to recrystallization annealing at 580

°C for 60 minutes. After annealing, surface of the samples is brushed for elimination of

possible surface defects propagation during cold working process. After first run of cold

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drawing the wire with diameter of 4.47 mm was obtained. Followed by three more runs the

wire with ø 4.02 mm, 3.61 mm and 3.22 mm was produced. Between last two runs (ø 3.61

mm and 3.22 mm) the recrystallization annealing at 580 °C for 60 minutes was performed.

The exact procedure of plastic deformation process can be seen in Table 1. Samples selected

for investigation were in as-cast state (Figure 1) and after cold working process with

dimensions ø 4.47 mm and ø 3.22 mm (Figure 4), marked bold and underlined in the Table 1.

Insight into samples microstructure was obtained by optical microscopy (OM) equipped with

digital camera and scanning electron microscopy (SEM) along with energy dispersive x-ray

spectroscopy (EDS). The alloys hardness was determined by Vickers method.

Figure 1. Photograph of CuAlMn shape memory alloy bar ø 8 mm after casting

Table 1. Procedure of plastic deformation process on CuAlMn SMA bars

Deformation process Dimensions (mm) Shematic illustration of

crossection

Sample in as-cast state

HOT WORKING PROCESS - hot rolling and forging

Hot rolling (880 – 900 °C)

2 runs 6.10x8.50

Hot forging (880 – 900 °C) in a

profiled tool

Square side length

6.00

Hot rolling (880 – 900 °C)

1 run 4.50x9.50

Hot forging (880 – 900 °C) in a

profiled tool

Square side length

5.20

Hot rolling (880 – 900 °C)

1 run 4.00x8.70

Hot forging (880 – 900 °C) in a

profiled tool

Square side length

4.60

Hot forging (880 – 900 °C) in a

profiled tool

Square side length

4.80

COLD WORKING PROCESS - cold drawing

Cold drawing Ø 4.47

Cold drawing Ø 4.02

Cold drawing Ø 3.61

Annealing at 580 °C/60’

Cold drawing Ø 3.22

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Figure 2. Schematic illustration of a profiled forging tool

Figure 3. Photograph of CuAlMn shape memory alloy bar after first run of

hot rolling and forging

Figure 4. Photograph of CuAlMn shape memory alloy wire ø 4.47 mm (a) and ø 3.22 mm (b)

RESULTS AND DISCUSSION

By hot and cold plastic deformation process CuAlMn shape memory alloy wire was

successfully produced. The ductility as a useful property of this cooper based shape memory

alloy enables exhibition of better pseudoelasticity and therefore better hot or cold

workability. It has been reported [8-11] that alloying additions play a very significant role in

the properties of Cu-based shape memory alloys and required properties can be achieved by

proper designing/selection of the alloying elements.

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Figure 5 and 6 shows results of metallographic analysis by OM and SEM method of CuAlMn

selected samples.

Figure 5. Optical micrographs of CuAlMn SMA in as-cast state (a),

after cold drawing: ø 4.47 mm (b), ø 3.22 mm (c)

As can be seen, the CuAlMn as-cast bar has two-phase (α+β) microstructure (Figure 5a and

6a). It is known that in vertical section of phase diagram of Cu-Al-10 at.% Mn the single

phase region is broadened by addition of Mn and + microstructure exists [12]. Grain

structure with α+β phases a prerequisite for martensite formation after quenching. This

clearly indicates that all the alloys have potential to exhibit the shape memory behaviour

[13].

The influence of plastic deformation process can be seen on microstructures at the obtained

ø 4.47 mm and ø 3.22 mm wires after cold working (Figure 5b, 5c, 6b and 6c). In both cases

after cold working process the martensite appears in some places inside the microstructure.

Considering that the β phase exists in the alloy in as-cast state, during plastic deformation

process transforms into the martensite, probably came to appearance of stress-induced

martensite. The stress induced martensite transformation occurs during loading under the

almost constant stress [14].

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Figure 6. SEM micrographs of CuAlMn SMA in as-cast state (a),

after cold drawing: ø 4.47 mm (b), ø 3.22 mm (c)

Figures 7 and 8 shows SEM micrographs along with the marked positions for EDS analysis of

CuAlMn wire ø 4.47 mm and ø 3.22 mm, respectively. The results of the EDS analysis for cold

drawn wire with diameter ø 4.47 mm show the difference between position 1 which shows

higher amount of aluminum (7.45 wt.%) in comparison to positions 2 and 3 with amount of

aluminum of (5.30 and 5.03 wt. %), Figure 7 and Table 2. Similar composition difference is

noticed for wire with ø 3.22 mm, Figure 8 and Table 3. The difference between positions 1

and 2 has higher amount of aluminum (6.93 and 6.76 wt. %) in comparison to position 3 with

amount of aluminum of (4.92 wt. %). It can be assumed that the aluminum enriched phase

presents α phase. Sutou et al. [2] reported existence of two-phase microstructure

(martensite + ) in Cu-Al-Mn-Ni-Si alloy after heat treatment at 850 °C. Due to the fact that

the samples between the cold drawing runs were heat treated at 580 °C/60 minutes, the

martensite + α microstructure is possible.

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Figure 7. SEM micrograph of CuAlMn SMA wire ø 4.47 mm

Table 2. Chemical composition of CuAlMn SMA wire ø 4.47 mm positions

marked at the Fig.7, wt. %

Cu Al Mn

Position 1 82.74 7.45 9.81

Position 2 86.27 5.30 8.43

Position 3 86.47 5.03 8.50

Position 4 86.16 5.17 8.68

Figure 8. SEM micrograph of CuAlMn SMA wire ø 3.22 mm

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Table 3. Chemical composition of CuAlMn SMA wire ø 3.22 mm positions

marked at the Figure 8, wt. %

Cu Al Mn

Position 1 82.66 6.93 10.41

Position 2 83.17 6.76 10.09

Position 3 86.63 4.92 8.45

The hardness values of the investigated samples are given as mean value of three

measurements and the results can be seen at Figure 9. It is obvious that the hardness of the

alloy increases through the process of cold drawing. The hardness of the alloy in as-cast

state was 268 HV 0.05. Increase in alloys hardness is noticed for wire with ø 4.47 mm (318

HV 0.05) and for wire with ø 3.22 mm (341 HV 0.05), respectively.

Figure 9. Hardness of CuAlMn shape memory alloy before and after cold working process

CONCLUSIONS

With hot and cold plastic deformation process it was successfully produced the CuAlMn

shape memory wire with ø 4.47 mm and ø 3.22 mm in diameter from continuously casted ø

8mm CuAlMn shape memory alloy bar. From the results of microstructural characterization

and hardness measurements can be withdrawn following conclusions:

- From the optical and SEM micrographs obtained grain structure with α+β phases is

visible in the as-cast condition of the CuAlMn shape memory alloy. This

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microstructure is a prerequisite for martensite formation after quenching indicating

that the alloy has potential to exhibit the shape memory behaviour.

- In some places the martensite formation is observed in CuAlMn alloy wires (ø 4.47

mm and ø 3.22 mm) produced by cold drawing process. During hot and cold working

process appear favorable conditions for appearance of stress induced martensite.

- The results of EDS analysis for cold drawn wires with diameter ø 4.47 mm and ø 3.22

mm shows the difference between the positions enriched with aluminum content

indicating the existence of the α phase in the microstructure.

- The hardness of the alloy increases through the process of cold drawing from 268 HV

0.05 in as-cast state to 318 HV 0.05 wire with ø 4.47 mm and 341 HV 0.05 for wire

with ø 3.22 mm.

REFERENCES

[1] Q. Wang, F. Han, C. Cui, S. Bu, L. Bai, Effect of ageing on the reverse martensitic phase

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[2] Y. Sotou, N. Koeda, T. Omori, R. Kainuma, K. Ishida, Effects of aging on stress-induced

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Materialia, 57(2009), pp. 5759-5770.

[3] T. Omori, N. Koeda, Y. Sotou, R. Kainuma, K. Ishida, Superplasticity of Cu-Al-Mn-Ni shape

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[9] U. S. Mallik, V. Sampath, Effect of composition and ageing on damping characteristics of

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[10] U. Arlica, H. Zak, B. Weidenfeller, W. Riehemann, Impact of alloy composition and

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